WO2014002428A1 - 耐パウダリング性に優れた合金化溶融亜鉛めっき鋼板 - Google Patents

耐パウダリング性に優れた合金化溶融亜鉛めっき鋼板 Download PDF

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WO2014002428A1
WO2014002428A1 PCT/JP2013/003790 JP2013003790W WO2014002428A1 WO 2014002428 A1 WO2014002428 A1 WO 2014002428A1 JP 2013003790 W JP2013003790 W JP 2013003790W WO 2014002428 A1 WO2014002428 A1 WO 2014002428A1
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steel sheet
plating layer
powdering resistance
mass
crystal grains
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PCT/JP2013/003790
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English (en)
French (fr)
Japanese (ja)
Inventor
洋一 牧水
善継 鈴木
永野　英樹
長滝　康伸
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Ｊｆｅスチール株式会社
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Application filed by Ｊｆｅスチール株式会社 filed Critical Ｊｆｅスチール株式会社
Priority to EP13809989.0A priority Critical patent/EP2865780B1/en
Priority to JP2014522411A priority patent/JP5907263B2/ja
Priority to KR1020147034802A priority patent/KR101731693B1/ko
Priority to CN201380033876.XA priority patent/CN104411857B/zh
Priority to US14/408,123 priority patent/US9828663B2/en
Publication of WO2014002428A1 publication Critical patent/WO2014002428A1/ja

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    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/06—Zinc or cadmium or alloys based thereon
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
    • B32B15/013—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of an iron alloy or steel, another layer being formed of a metal other than iron or aluminium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0478—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing involving a particular surface treatment
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C18/00—Alloys based on zinc
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/26—After-treatment
    • C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/26—After-treatment
    • C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
    • C23C2/29—Cooling or quenching
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
    • C23C2/36—Elongated material
    • C23C2/40—Plates; Strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2251/00—Treating composite or clad material
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12785—Group IIB metal-base component
    • Y10T428/12792—Zn-base component
    • Y10T428/12799—Next to Fe-base component [e.g., galvanized]

Definitions

  • the present invention relates to an alloyed hot-dip galvanized steel sheet, and more particularly to an alloyed hot-dip galvanized steel sheet having excellent powdering resistance.
  • alloyed hot-dip galvanized steel sheets are heated after hot-rolling or cold-rolling steel sheets are recrystallized and annealed in a CGL (continuous hot-dip galvanizing line) annealing furnace.
  • a CGL continuous hot-dip galvanizing line
  • an alloying reaction occurs in which Fe in the steel plate and Zn in the plating layer diffuse, thereby forming an Fe—Zn alloy phase.
  • This Fe—Zn alloy phase is usually a film composed of a ⁇ phase, a ⁇ 1 phase, and a ⁇ phase.
  • the concentration decreases, that is, the hardness and melting point tend to decrease in the order of ⁇ phase ⁇ ⁇ 1 phase ⁇ ⁇ phase.
  • the concentration is designed to be higher.
  • Patent Document 1 in order to achieve both slidability and powdering resistance, a method of applying a hard Fe-based alloy as a second layer to the upper layer by an electroplating method is employed.
  • a treatment facility such as electroplating is required, which is not only undesirable from the viewpoint of facilities and economy, but the improvement effect on fundamental powdering resistance is I can't expect it.
  • the present invention has been made in view of such circumstances, and restricts the content of elements in steel such as Si and P, which are useful for improving the strength of a steel sheet, in order to satisfy the necessary properties of the material, to a low concentration.
  • Another object of the present invention is to provide an alloyed hot-dip galvanized steel sheet having excellent powdering resistance at the time of press work without causing an increase in cost due to complicated processes.
  • the chemical components of the galvannealed steel sheet are: C: 0.030 to 0.200% by mass, Si: 0.5 to 2.0% by mass, Mn: 1.0 to 3.0% by mass P: 0.025% by mass or less, S: 0.010% by mass or less, and the balance is Fe and inevitable impurities, wherein any one of [1] to [3] An alloyed hot-dip galvanized steel sheet with excellent powdering resistance.
  • an alloyed hot-dip galvanized steel sheet having excellent powdering resistance can be obtained.
  • FIG. 1 is a cross-sectional photograph of a plating layer.
  • FIG. 2 is a view obtained by binarizing the photograph of FIG. 1 in order to obtain the plating layer cross-sectional area.
  • FIG. 3 is a diagram obtained by binarizing the photograph of FIG. 1 in order to obtain the crystal grain cross-sectional area of the ground iron in the plating layer.
  • the present inventors investigated the powdering resistance of various galvannealed steel sheets.
  • the steel sheet having a low Fe content in the plating layer had good powdering resistance because it had less formation of a hard and brittle ⁇ phase at the plated steel sheet interface.
  • the steel sheet having a low Fe content in the plating layer had good powdering resistance because it had less formation of a hard and brittle ⁇ phase at the plated steel sheet interface.
  • an alloyed hot-dip galvanized steel sheet having a high Fe content in the plating layer there are steel sheets that exhibit good powdering resistance. I understood that.
  • FIG. 1 is an example of a cross-sectional SEM image of a plating layer in which ground crystal grains are taken into the plating layer.
  • the crystal grains of the ground iron in the plating layer can be clearly observed as shown in FIG.
  • the plating layer is processed by binarization processing (processing for converting the brightness of each pixel into two values of black and white by a predetermined threshold) as shown in FIG.
  • the cross-sectional area of the crystal grains of the ground iron in the plating layer is obtained by binarizing as shown in FIG.
  • the cross-sectional area ratio of the crystal grain of the base iron which occupies in a plating layer can be calculated
  • the contrast of the backscattered electron image varies depending on the atomic number, it is possible to clearly distinguish the plated layer portion and the ground iron portion by the difference in contrast.
  • the present invention is characterized in that the ground iron crystal grains are incorporated in the plating layer at a ratio of the cross-sectional area ratio of 2.0 to 15.0%. If it is less than 2.0%, the effect of suppressing the progress of cracks in the plating layer is small, so the effect of improving the powdering resistance is small. In addition to the saturation of the effect when it exceeds 15.0%, the occurrence of red rust due to the corrosion of the ground iron grains incorporated in the plating layer when used in an automobile body There is a concern that there will be more.
  • the Fe content in the plating layer is measured by dissolving the plating layer with hydrochloric acid containing an inhibitor and obtaining the Fe amount by a method such as ICP (inductively coupled plasma) analysis.
  • the Fe content is preferably 10 to 20% by mass from the viewpoint of improving powdering resistance.
  • the Fe content is less than 10% by mass, the amount of the ground iron crystal grains taken into the plating layer is small, and the effect of suppressing the progress of cracks in the plating layer is small. small.
  • the effect of improving the powdering resistance due to the incorporation of crystal grains of the ground iron is saturated, and in addition to the occurrence of red rust accompanying the corrosion of the crystal grains of the ground iron, Since the formation of the hard and brittle ⁇ phase formed at the interface between the plating layer and the base iron also increases, the effect of improving the powdering resistance is small.
  • Si, Mn or the like as an internal oxide at the grain boundary of the steel sheet surface layer. If the internal oxide is formed at the grain boundary of the steel sheet surface layer, the alloying reaction of Fe-Zn takes place preferentially from the grain boundary in the subsequent alloying treatment step, and as a result, crystal grains of the iron Is taken into the plating layer.
  • the plating adhesion amount is preferably 20 to 120 g / m 2 per side. If it is less than 20 g / m 2 , it becomes difficult to ensure good corrosion resistance. If it exceeds 120 g / m 2 , the amount of plating itself that peels off in a powder state at the time of compressive deformation increases, so that the effect of improving the powdering resistance is small.
  • the content of each element of the steel component composition and the unit of the content of each element of the plating layer component composition are “mass%”, and are simply “%” unless otherwise specified. .
  • Si 0.5 to 2.0% Si is an element effective for strengthening steel and obtaining a good material. If it is less than 0.5%, it is difficult to realize the state of the plating layer as in the present invention by utilizing the formation of the internal oxide. On the other hand, if it exceeds 2.0%, appearance defects such as non-plating and uneven alloying are likely to occur during the hot dip galvanizing process. Therefore, the Si content is desirably 0.5 to 2.0%.
  • Mn 1.0 to 3.0%
  • Mn is also an effective element for increasing the strength of steel. However, if it is less than 1.0%, it is difficult to take in the crystal grains of the base iron into the plating layer by utilizing the formation of the internal oxide. On the other hand, if it exceeds 3.0%, appearance defects such as non-plating and uneven alloying are likely to occur during the hot dip galvanizing process. Therefore, the Mn content is desirably 1.0 to 3.0%.
  • the following elements may be contained as necessary.
  • C 0.030 to 0.200%
  • C is an element necessary for controlling the steel structure. If it is 0.030% or less, it is difficult to ensure a desired strength. Moreover, when it exceeds 0.200%, weldability may deteriorate. Therefore, the C content is preferably 0.030 to 0.200%.
  • P 0.025% or less P is inevitably contained. If it exceeds 0.025%, weldability may deteriorate. Therefore, the P content is preferably 0.025% or less.
  • S 0.010% or less S is an element inevitably contained. No lower limit is specified. However, if it is contained in a large amount, the weldability may deteriorate, so 0.010% or less is preferable.
  • Al 0.01 to 0.10%
  • B 0.001 to 0.005%
  • Nb 0.005 to 0.050%
  • Ti 0.005 To 0.050%
  • Cr 0.05 to 1.00%
  • Mo 0.05 to 1.00%
  • Cu 0.05 to 1.00%
  • Ni 0.05 to 1.00%
  • elements selected from among them may be contained as necessary. The reasons for limitation are as follows.
  • Al is less than 0.01%, it is difficult to obtain a deoxidation effect in the steel making process, and if it exceeds 0.10%, the slab quality is deteriorated.
  • Nb is less than 0.005%, the effect of adjusting the strength is difficult to obtain, and if it exceeds 0.050%, the cost increases.
  • Ti is less than 0.005%, the effect of adjusting the strength is difficult to obtain, and if it exceeds 0.050%, the plating adhesion may be deteriorated.
  • Ni is less than 0.05%, the effect of promoting the formation of the residual ⁇ phase is difficult to obtain, and when it exceeds 1.00%, the cost increases. Needless to say, when it is determined that it is not necessary to improve the mechanical properties, it is not necessary to contain it.
  • the remainder other than the above is Fe and inevitable impurities.
  • Si, Mn and the like are formed as internal oxides at the grain boundary of the steel sheet surface layer, and further, an acidic solution such as hydrochloric acid is used to form the grain boundary. There is a way to erode. If the internal oxide is formed at the grain boundary of the steel sheet surface layer, the alloying reaction of Fe-Zn takes place preferentially from the grain boundary in the subsequent alloying treatment step, and as a result, crystal grains of the iron Is taken into the plating layer.
  • the steel sheet is oxidized in advance before hot galvanizing, and the surface layer is oxidized by hot rolling.
  • a method of performing a reduction annealing after forming an iron layer a method of controlling a dew point in the atmosphere in an annealing step before a hot dip galvanizing process, and the like.
  • the oxide scale formed on the surface of the steel plate in the hot rolling process becomes an oxygen source, and in the process of cooling after being rolled up, Si and Mn are internally oxidized. It can be formed on the surface layer of a steel sheet as a product. Since the oxidation reaction is accelerated at higher temperatures, it is desirable to wind up at 600 ° C. or higher.
  • the iron oxide layer formed on the surface layer becomes a supply source of oxygen, and in the reduction annealing step, Si It is possible to form Mn as an internal oxide on the surface layer of the steel sheet. In order to increase the amount of oxygen serving as the supply source, it is necessary to form sufficient iron oxide in advance. Therefore, it is desirable to oxidize the steel plate in advance in an oxidizing atmosphere at a temperature of 700 ° C. or higher.
  • the present invention will be specifically described based on examples.
  • the steel sheet having the component composition shown in Table 1 as a test material
  • the steel sheet was heated in an oxidizing atmosphere in advance to form iron oxide on the surface, followed by reduction annealing, pickling treatment, Hot dip galvanizing treatment and alloying treatment were performed.
  • Oxidation is performed by using a direct burner to set the air / fuel ratio to 1 or more, and to change the maximum temperature (oxidation temperature) by controlling the output of the direct fire burner.
  • nitrogen gas was cooled without holding.
  • reduction annealing was performed using an infrared heating furnace in a 10 vol% hydrogen + nitrogen atmosphere (dew point: ⁇ 35 ° C.) under conditions of a plate temperature of 820 ° C. and a holding time of 30 seconds.
  • the plating conditions were a 460 ° C. zinc plating bath containing 0.14% by mass of Al (Fe saturation), an intrusion plate temperature: 460 ° C., and an immersion time: 1 second.
  • the amount of adhesion was adjusted with a nitrogen gas wiper. About some, after cooling with nitrogen gas after reductive annealing, after performing the pickling process by being immersed in hydrochloric acid containing an inhibitor for 20 seconds, the hot dip galvanizing process was implemented.
  • the obtained hot-dip galvanized steel sheet was subjected to alloying treatment at 500 to 600 ° C. for 15 seconds in an induction heating furnace.
  • the plating adhesion amount was determined by the weight difference before and after the plating layer was dissolved with hydrochloric acid containing an inhibitor. Further, the Fe content in the hydrochloric acid in which the plating layer was dissolved was measured by ICP analysis for the Fe content in the plating layer.
  • the method for measuring the cross-sectional area ratio of the crystal grains of the ground iron incorporated in the plating layer and the method for evaluating the powdering resistance are as follows.
  • a cellophane tape having a width of 24 mm is pressed against the inner side (compression side) of the bent part when the galvannealed steel sheet manufactured by the above method is bent at an angle of 60 ° and pulled apart.
  • the amount of zinc adhering to the 40 mm long portion of the cellophane tape was measured by Zn count by fluorescent X-ray. Evaluation was made in light of the following criteria. A score of 3 or higher was accepted.
  • Fluorescent X-ray Zn count number Rating 0 to less than 1500: 5 (good) Less than 1500-3000: 4 3000 to less than 4000: 3 4000 to less than 5000: 2 5000 or more: 1 (poor) The production conditions and the results obtained are shown in Table 2.
  • the alloyed hot-dip galvanized steel sheet having the plating layer of the present invention has good powdering resistance.
  • the alloyed hot-dip galvanized steel sheet outside the scope of the present invention has poor powdering resistance.
  • the alloyed hot-dip galvanized steel sheet of the present invention can be used as an alloyed hot-dip galvanized steel sheet having excellent powdering resistance.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Organic Chemistry (AREA)
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  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
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PCT/JP2013/003790 2012-06-25 2013-06-18 耐パウダリング性に優れた合金化溶融亜鉛めっき鋼板 WO2014002428A1 (ja)

Priority Applications (5)

Application Number Priority Date Filing Date Title
EP13809989.0A EP2865780B1 (en) 2012-06-25 2013-06-18 Galvannealed steel sheet with excellent anti-powdering properties
JP2014522411A JP5907263B2 (ja) 2012-06-25 2013-06-18 耐パウダリング性に優れた合金化溶融亜鉛めっき鋼板
KR1020147034802A KR101731693B1 (ko) 2012-06-25 2013-06-18 내파우더링성이 우수한 합금화 용융 아연 도금 강판
CN201380033876.XA CN104411857B (zh) 2012-06-25 2013-06-18 抗粉化性优良的合金化热镀锌钢板
US14/408,123 US9828663B2 (en) 2012-06-25 2013-06-18 Galvannealed steel sheet with excellent anti-powdering property

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Application Number Priority Date Filing Date Title
JP2012-141531 2012-06-25
JP2012141531 2012-06-25

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WO2014002428A1 true WO2014002428A1 (ja) 2014-01-03

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US (1) US9828663B2 (ko)
EP (1) EP2865780B1 (ko)
JP (1) JP5907263B2 (ko)
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EP2865780A4 (en) 2015-04-29
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EP2865780A1 (en) 2015-04-29
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